EP1753885A1 - Procede de production d'une feuille de brasage d'alliage d'aluminium, et feuille de brasage d'alliage d'aluminium obtenue par ce procede - Google Patents

Procede de production d'une feuille de brasage d'alliage d'aluminium, et feuille de brasage d'alliage d'aluminium obtenue par ce procede

Info

Publication number
EP1753885A1
EP1753885A1 EP05746552A EP05746552A EP1753885A1 EP 1753885 A1 EP1753885 A1 EP 1753885A1 EP 05746552 A EP05746552 A EP 05746552A EP 05746552 A EP05746552 A EP 05746552A EP 1753885 A1 EP1753885 A1 EP 1753885A1
Authority
EP
European Patent Office
Prior art keywords
alloy
sheet
brazing
process according
core
Prior art date
Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
Granted
Application number
EP05746552A
Other languages
German (de)
English (en)
Other versions
EP1753885B1 (fr
EP1753885B2 (fr
Inventor
Scott William Haller
Job Anthonius Van Der Hoeven
Klaus Vieregge
Achim BÜRGER
Sampath Desikan
Current Assignee (The listed assignees may be inaccurate. Google has not performed a legal analysis and makes no representation or warranty as to the accuracy of the list.)
Novelis Koblenz GmbH
Original Assignee
Corus LP
Corus Aluminium Walzprodukte GmbH
Priority date (The priority date is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the date listed.)
Filing date
Publication date
Family has litigation
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Application filed by Corus LP, Corus Aluminium Walzprodukte GmbH filed Critical Corus LP
Priority to EP05746552.8A priority Critical patent/EP1753885B2/fr
Publication of EP1753885A1 publication Critical patent/EP1753885A1/fr
Publication of EP1753885B1 publication Critical patent/EP1753885B1/fr
Application granted granted Critical
Publication of EP1753885B2 publication Critical patent/EP1753885B2/fr
Active legal-status Critical Current
Anticipated expiration legal-status Critical

Links

Classifications

    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22F—CHANGING THE PHYSICAL STRUCTURE OF NON-FERROUS METALS AND NON-FERROUS ALLOYS
    • C22F1/00—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working
    • C22F1/04—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of aluminium or alloys based thereon
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22F—CHANGING THE PHYSICAL STRUCTURE OF NON-FERROUS METALS AND NON-FERROUS ALLOYS
    • C22F1/00—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working
    • C22F1/04—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of aluminium or alloys based thereon
    • C22F1/053—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of aluminium or alloys based thereon of alloys with zinc as the next major constituent
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
    • B21B—ROLLING OF METAL
    • B21B3/00—Rolling materials of special alloys so far as the composition of the alloy requires or permits special rolling methods or sequences ; Rolling of aluminium, copper, zinc or other non-ferrous metals
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C21/00—Alloys based on aluminium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C21/00—Alloys based on aluminium
    • C22C21/10—Alloys based on aluminium with zinc as the next major constituent
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C21/00—Alloys based on aluminium
    • C22C21/12—Alloys based on aluminium with copper as the next major constituent
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C21/00—Alloys based on aluminium
    • C22C21/12—Alloys based on aluminium with copper as the next major constituent
    • C22C21/14—Alloys based on aluminium with copper as the next major constituent with silicon
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C21/00—Alloys based on aluminium
    • C22C21/12—Alloys based on aluminium with copper as the next major constituent
    • C22C21/16—Alloys based on aluminium with copper as the next major constituent with magnesium

Definitions

  • the invention relates to a process for producing an Al-Mn alloy sheet with improved liquid film migration resistance when used as core alloy in brazing sheet materials.
  • the invention further relates to an AI-Mn alloy sheet produced according to said process and to the use of said alloy sheet.
  • LFM the phenomenon known as 'Liquid Film Migration' or LFM
  • core dissolution or "core penetration” or “core erosion”.
  • core erosion we refer to all these terminologies.
  • a core alloy of a brazing sheet product requires a good combination of strength and formability.
  • the susceptibility to LFM has to be at a sufficiently low level to ensure adequate corrosion resistance and brazeability.
  • Higher strength can be obtained by alloying with elements such as silicon, manganese, chromium, zirconium or vanadium.
  • these alloying elements also increase the susceptibility to LFM.
  • the use of a non O-temper, such as H14- temper or H24-temper has also been suggested to reduce the susceptibility to LFM.
  • these tempers effectively reduce the LFM, formability of the brazing sheet product is often compromised.
  • a process for producing an Al-Mn alloy sheet with improved liquid film migration resistance when used as core alloy in brazing sheet comprising the steps of:
  • composition comprising (in weight percent): o 0.5 ⁇ Mn ⁇ 1.7, preferably 0.6 - 1.7, o 0.06 ⁇ Cu ⁇ 1.5, preferably 0.2 to 1.5, o Si ⁇ 1.3, preferably Si ⁇ 0.8, more preferably Si ⁇ 0.3, o Mg ⁇ 0.25 o Ti ⁇ 0.2 o Zn ⁇ 2.0 o Fe ⁇ 0.5 o at least one element of the group of elements consisting of 0.05 ⁇ Zr ⁇ 0.25 and 0.05 ⁇ Cr ⁇ 0.25 o other elements ⁇ 0.05 each and total ⁇ 0.20, balance Al.
  • the chromium strengthens the alloy, whereas the recrystallisation of the alloy results in adequate formability.
  • the Cr and/or Zr content is at least 0.08%.
  • the maximum magnesium content is 0.1%, preferably the maximum magnesium content is 0.05%.
  • the magnesium content should be as low as possible to avoid the deleterious effect of magnesium on the flux that is used during Controlled Atmosphere Brazing.
  • the copper content is from 0.7 to 1.2 %.
  • the manganese content is from 0.7 to 1.4 %.
  • the maximum zinc content is preferably 0.4% to prevent the core alloy being excessively anodic in certain applications.
  • the iron content is preferably below 0.35% to prevent the formation of undesirable large iron containing intermetallics during industrial casting practices.
  • the homogenisation temperature is between about 530 °C and 620°C, preferably between 530 and 595 °C, preferably for between 1 to 25 hours, more preferably for between 10 to 16 hours, and wherein the pre-heat temperature is between about 400 °C and 530°C, preferably between 420 and 510 °C, preferably for between 1 to 25 hours, more preferably for between 1 and 10 hours.
  • the alloys according to the invention it appears that the best compromise between the strength, formability, susceptibility to LFM and corrosion resistance was found when the homogenisation temperature and time and the pre-heat temperature and time was chosen within the given boundaries and that a particularly interesting compromise was obtained when processing the alloy according to the abovementioned preferred temperatures and times.
  • the process according to the invention also comprises recrystallisation annealing after cold rolling at an annealing temperature-annealing time combination sufficient for promoting essentially full recrystallisation of the Al-Mn alloy. In this condition the highest formability is reached.
  • the maximum silicon content of the Al-Mn alloy is 0.3 % in weight. In a preferable embodiment of the invention the maximum silicon content of the Al-Mn alloy is 0.15 % in weight.
  • Silicon is known to increase the susceptibility to LFM. Consequently, the silicon content is to be chosen as low as possible. However, the inventors found that when using a silicon content of up to 0.3 % but preferably of up to 0.15 % that an adequate combination of susceptibility to LFM and strength was obtained.
  • Cr ⁇ 0.18%, preferably at least 0.06%, more preferably 0.08% ⁇ Cr ⁇ 0.15%, even more preferably 0.08% ⁇ Cr ⁇ 0.12%.
  • the Cr-level exceeds 0.18%, casting of the Al-Mn alloy becomes very difficult as a result of the formation of large intermetallics. Casting the Al-Mn with Cr-contents of below 0.15% or below 0.12 causes no problems.
  • the process also comprises cladding the Al-Mn alloy on at least one side with an AA4000-series or Al-Si brazing alloy optionally comprising up to 2.0 % Zn. Cladding may for instance be performed by roll-bonding or any other known technique such as spray cladding or cast cladding.
  • the invention is also embodied in a sheet produced according to the process as described hereinabove, wherein the pre-braze elongation is at least 18%, preferably at least 19 %, more preferably at least 21 % and/or a pre-braze n-value of at least 0.270, and/or a post-brazing tensile strength of at least 140 MPa, preferably of at least 150 MPa.
  • the elongation is measured over a gauge length of 80 mm, also denoted as A80.
  • the post-braze coupon SWAAT lifetime measured in terms of time to perforation in days and, when tested according to ASTM G85 A3, is at least 15 days, preferably at least 20 days without perforation.
  • the low susceptibility to LFM is reflected in an improved resistance against corrosion in a formed heat exchanger component after brazing.
  • the sheet as described hereinabove is applied as a core in brazing sheet with or without a non-brazing liner or waterside liner alloy such as an AA7072, an AA1145 or an AA 3005 or Al-Mn type alloys containing Zn in the range 0.5-5.0%, preferably in the range 0.5-2.5%, in folded tubes or for applications which are used under similar conditions.
  • the requirements as to strength, formability, LFM susceptibility and corrosion resistance are particularly relevant for the application of the sheet as a core in a brazing sheet, for instance for application in heat exchangers utilising folded tubes.
  • the sheet materials produced according to the process described hereinabove are particularly suitable for use as a core alloy in brazing sheet materials intended for manufacturing of components of tube-fin type heat exchangers such as radiators, heater cores and condensers, or for manufacturing of components of plate-fin type heat exchanger such as evaporator or oil cooler core plates or tanks of radiators or heater cores as a core alloy in brazing fin stock materials intended for manufacturing of components for heat exchangers.
  • a specific embodiment of the present invention will now be explained by the following non-limitative examples.
  • alloys 1-4 were subjected to a homogenisation treatment at various temperatures for various times. Subsequently the alloys were clad on both sides with AA4045, 10% of the thickness on each side, followed by a preheat prior to hot rolling at various temperatures for various times, hot-rolling to 6.5 mm followed by an inter anneal at 350 °C for 3 hours, a first cold rolling to 2.3 mm, again followed by an inter anneal at 350 °C for 3 hours and a second cold rolling to a final gauge of 0.5 mm. The alloy was subjected to a recrystallisation annealing treatment to promote essentially full recrystallisation. To test the LFM behaviour, the materials were stretched between 2 and 10%.
  • the stretch level that showed the deepest penetration was used for the LFM data in Table 2.
  • Alloy 5 and 6 were clad on both sides with AA4045, 10% of the thickness on each side, followed by a preheat prior to hot rolling, and subsequently hot rolled to 3.5 mm and cold-rolled to 0.41 mm without inter annealing. After cold-rolling the material was subjected to a recrystallisation annealing treatment to promote essentially full recrystallisation. The LFM behaviour was tested as described above. The results are presented in Table 2.
  • the alloy designated 'standard' is an alloy which is used for LFM-critical applications.
  • n-value can be used as an alternative indicator of formability.
  • An n-value of at least 0.270 indicates a good formability in view of the minimum strength requirement of at least 140 MPa.
  • the alloys according to the invention such as alloy 2-6 in Table 2, provide equal LFM-performance, but with significantly higher post-braze tensile properties.
  • Another particular alloy which can be produced using the method according to the invention has the following compositional ranges, in wt.%: Si 0.8 -1.0, and typically about 0.9 • Fe 0.25 - 0.4, and typically about 0.35 Cu 0.25 - 0.45, and typically about 0.40 Mn 0.55 - 0.9, and typically about 0.85 Mg 0.1 - 0.22, and typically about 0.15 Zn 0.06 - 0.10, and typically about 0.08 • Cr 0.06-0.10, and typically about 0.08 Zr 0.06 - 0.10, and typically about 0.08, balance aluminium and inevitable impurities.
  • the alloy can be used amongst others for tube plate, side supports and header tanks. It is of course to be understood that the present invention is not limited to the described embodiments and examples described above, but encompasses any and all embodiments within the scope of the description and the following claims.

Landscapes

  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Mechanical Engineering (AREA)
  • Materials Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Physics & Mathematics (AREA)
  • Thermal Sciences (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • Laminated Bodies (AREA)
  • Details Of Heat-Exchange And Heat-Transfer (AREA)
  • Continuous Casting (AREA)

Abstract

L'invention concerne un procédé de production d'une feuille d'alliage Al-Mn présentant une résistance accrue à la migration de film liquide, lorsque cet alliage de noyau est utilisé en feuille de brasage. Ce procédé consiste à: couler un lingot présentant une composition comprenant (en pourcentage en poids): 0,5< Mn=1,7; 0,06<Cu=1,5; Si =1,3; Mg=0,25; Ti<0,2; Zn=2,0; Fe=0,5; au moins un élément du groupe des éléments comprenant: 0,05<Zr=0,25 et 0,05<Cr=0,25; d'autres éléments étant chacun inférieur à 0,05 et au total étant inférieur à 0,20; le reste étant Al. Puis, le procédé comprend les étapes suivantes: homogénéisation et préchauffage, laminage à chaud, laminage à froid (comprenant des recuits intermédiaires, le cas échéant), la température d'homogénéisation étant d'au moins 450 °C, pendant une durée d'au moins une heure, suivi d'un refroidissement par air à au moins 20 °C/heure, la température de préchauffage étant d'au moins 400 °C, pendant au moins 30 minutes.
EP05746552.8A 2004-05-26 2005-05-25 Procede de production d'une feuille de brasage d'alliage d'aluminium, et feuille de brasage d'alliage d'aluminium obtenue par ce procede Active EP1753885B2 (fr)

Priority Applications (1)

Application Number Priority Date Filing Date Title
EP05746552.8A EP1753885B2 (fr) 2004-05-26 2005-05-25 Procede de production d'une feuille de brasage d'alliage d'aluminium, et feuille de brasage d'alliage d'aluminium obtenue par ce procede

Applications Claiming Priority (5)

Application Number Priority Date Filing Date Title
EP04076545 2004-05-26
EP04076785 2004-06-18
EP04077623 2004-09-23
EP05746552.8A EP1753885B2 (fr) 2004-05-26 2005-05-25 Procede de production d'une feuille de brasage d'alliage d'aluminium, et feuille de brasage d'alliage d'aluminium obtenue par ce procede
PCT/EP2005/005751 WO2005118899A1 (fr) 2004-05-26 2005-05-25 Procede de production d'une feuille de brasage d'alliage d'aluminium, et feuille de brasage d'alliage d'aluminium obtenue par ce procede

Publications (3)

Publication Number Publication Date
EP1753885A1 true EP1753885A1 (fr) 2007-02-21
EP1753885B1 EP1753885B1 (fr) 2016-12-28
EP1753885B2 EP1753885B2 (fr) 2022-08-24

Family

ID=34968764

Family Applications (1)

Application Number Title Priority Date Filing Date
EP05746552.8A Active EP1753885B2 (fr) 2004-05-26 2005-05-25 Procede de production d'une feuille de brasage d'alliage d'aluminium, et feuille de brasage d'alliage d'aluminium obtenue par ce procede

Country Status (8)

Country Link
EP (1) EP1753885B2 (fr)
JP (1) JP5326123B2 (fr)
KR (1) KR101216246B1 (fr)
CN (1) CN1973056B (fr)
CA (1) CA2565978C (fr)
HU (1) HUE032303T2 (fr)
MX (1) MXPA06013571A (fr)
WO (1) WO2005118899A1 (fr)

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WO2015021383A1 (fr) * 2013-08-08 2015-02-12 Novelis Inc. Tôle à ailettes en alliage d'aluminium haute résistance pour échangeurs de chaleur
WO2015021244A1 (fr) * 2013-08-08 2015-02-12 Novelis Inc. Tôle à ailettes en alliage d'aluminium à haute résistance pour échangeur de chaleur
US9719156B2 (en) 2011-12-16 2017-08-01 Novelis Inc. Aluminum fin alloy and method of making the same
US11933553B2 (en) 2014-08-06 2024-03-19 Novelis Inc. Aluminum alloy for heat exchanger fins

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CN103122428A (zh) * 2011-11-18 2013-05-29 萨帕铝热传输(上海)有限公司 钎焊用铝合金复合管材及其制造方法
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CN103290283A (zh) * 2013-06-24 2013-09-11 靖江市新程汽车零部件有限公司 汽车排气管隔热板及其制造方法
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FR3018213B1 (fr) 2014-03-06 2016-10-21 Constellium France Tole de brasage a placages multiples
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ES2703557T5 (es) * 2014-09-12 2022-08-19 Novelis Inc Aleaciones para productos de aluminio altamente conformados y métodos para fabricarlos
CN105543575B (zh) * 2015-12-21 2017-11-28 无锡市世达精密焊管制造有限公司 一种富含硅、铜和钛元素的铝合金板锭及其制备方法
CN105648280A (zh) * 2016-01-22 2016-06-08 济南大学 一种铝单板用铸态合金材料及其制备方法
JP6604699B2 (ja) * 2016-03-31 2019-11-13 株式会社デンソー アルミニウム合金製クラッド材及びその製造方法
CN105886861B (zh) * 2016-05-12 2017-08-22 宝鸡石油钢管有限责任公司 一种铝合金连续管及其制造方法
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WO2020178507A1 (fr) * 2019-03-04 2020-09-10 Constellium Neuf-Brisach Bande en alliage d'aluminium pour la fabrication d'échangeurs de chaleur brasés
FR3093450A1 (fr) 2019-03-04 2020-09-11 Constellium Neuf-Brisach Bande en alliage d’aluminium pour la fabrication d’échangeurs de chaleur brasés
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Cited By (4)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US9719156B2 (en) 2011-12-16 2017-08-01 Novelis Inc. Aluminum fin alloy and method of making the same
WO2015021383A1 (fr) * 2013-08-08 2015-02-12 Novelis Inc. Tôle à ailettes en alliage d'aluminium haute résistance pour échangeurs de chaleur
WO2015021244A1 (fr) * 2013-08-08 2015-02-12 Novelis Inc. Tôle à ailettes en alliage d'aluminium à haute résistance pour échangeur de chaleur
US11933553B2 (en) 2014-08-06 2024-03-19 Novelis Inc. Aluminum alloy for heat exchanger fins

Also Published As

Publication number Publication date
HUE032303T2 (en) 2017-09-28
EP1753885B1 (fr) 2016-12-28
WO2005118899A1 (fr) 2005-12-15
JP2008500453A (ja) 2008-01-10
EP1753885B2 (fr) 2022-08-24
JP5326123B2 (ja) 2013-10-30
CN1973056A (zh) 2007-05-30
CN1973056B (zh) 2010-11-24
CA2565978C (fr) 2013-03-26
CA2565978A1 (fr) 2005-12-15
MXPA06013571A (es) 2007-03-15
KR101216246B1 (ko) 2012-12-28
KR20070058383A (ko) 2007-06-08

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